EP0188704B1 - Fiber reinforced metal composite material - Google Patents

Fiber reinforced metal composite material Download PDF

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Publication number
EP0188704B1
EP0188704B1 EP19850115192 EP85115192A EP0188704B1 EP 0188704 B1 EP0188704 B1 EP 0188704B1 EP 19850115192 EP19850115192 EP 19850115192 EP 85115192 A EP85115192 A EP 85115192A EP 0188704 B1 EP0188704 B1 EP 0188704B1
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EP
European Patent Office
Prior art keywords
composite material
fibers
fiber reinforced
metal composite
silicon
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP19850115192
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German (de)
English (en)
French (fr)
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EP0188704A3 (en
EP0188704A2 (en
Inventor
Atsuo Tanaka
Tadashi Dohnomoto
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Toyota Motor Corp
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Toyota Motor Corp
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Publication date
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Publication of EP0188704A2 publication Critical patent/EP0188704A2/en
Publication of EP0188704A3 publication Critical patent/EP0188704A3/en
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Publication of EP0188704B1 publication Critical patent/EP0188704B1/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C49/00—Alloys containing metallic or non-metallic fibres or filaments
    • C22C49/02—Alloys containing metallic or non-metallic fibres or filaments characterised by the matrix material
    • C22C49/04—Light metals
    • C22C49/06—Aluminium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/02—Light metals
    • F05C2201/021—Aluminium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2251/00—Material properties
    • F05C2251/04—Thermal properties
    • F05C2251/042—Expansivity
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/4998—Combined manufacture including applying or shaping of fluent material
    • Y10T29/49982—Coating
    • Y10T29/49986—Subsequent to metal working
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12486—Laterally noncoextensive components [e.g., embedded, etc.]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/12764—Next to Al-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/31504—Composite [nonstructural laminate]
    • Y10T428/31855—Of addition polymer from unsaturated monomers
    • Y10T428/31931—Polyene monomer-containing

Definitions

  • This invention concerns a fiber reinforced metal composite material which has a reduced thermal expansion coefficient while retaining good abrasion resistance and heat resistance.
  • Applications of this invention include compressor and engine parts, for example, vanes, rotors, swash plates and other parts of a compressor, parts of the pistons of an engine and the liners in engines or compressors.
  • Hyper-eutectic aluminium-silicon-type alloys comprising primary crystal silicon have hitherto been used in materials requiring abrasion resistance, heat resistance and a low thermal expansion coefficient, in addition to reduced weight.
  • the thermal expansion coefficient of the hyper-eutectic aluminium-silicon-type alloys is about 18x 10 -6 /°C. Therefore, they have not always been satisfactory when used as components for compressor vanes etc., particularly, those requiring a low thermal expansion coefficient.
  • fiber reinforced metal composite materials having abrasion resistance and a low thermal expansion coefficient i.e., composite materials in which the JIS-AC8A aluminium alloy having the composition AI-12% Si-1% Cu-2% Ni is reinforced with alumina-silica fibers, where this composite material is excellent in abrasion resistance, heat resistance and seizure resistance to suppress the thermal expansion by the fibers (refer to composite material disclosed in Japanese Patent Laid-Open No. 93837/1983).
  • EP-A-0 081 204 discloses a fiber reinforced metal composite material the metal matrix of which is an aluminium alloy of the AI-12% Si system (silumin) wherein primary crystal silicon is present.
  • the reinforcing fibers are alumina-based fibers containing preferably not more than 28% by weight of silica which are embedded in the metal matrix, the volume ratio of said alumina-based fibers in the total composite material being preferably 50%.
  • the object of the present invention is to provide a fiber reinforced metal composite material in which the thermal expansion coefficient is further reduced without affecting the merits of the composite material such as abrasion resistance, heat resistance and seizure resistance.
  • a fiber reinforced metal composite material having a metal matrix consisting of an aluminium-silicon-type alloy in which primary crystal silicon is dispersed, and reinforcing fibers embedded in said matrix comprising at least one member of the group consisting of alumina fibers and alumina-silica-type fibers with an average diameter of less than 10 pm, said metal matrix consisting of said aluminium-silicon-type alloy including 15 to 30% by weight of silicon enriched in primary crystal silicon and the volume ratio of said reinforcing fibers in the fiber reinforced metal composite material ranging from 5 to 15%.
  • alumina fibers and/or alumina-silica-type fibers with an average diameter of less than 10 11m are used.
  • Alumina fibers and alumina-silica-type fibers currently available can be employed.
  • the alumina content in the alumina-silica-type fibers is preferably not less than 40% by weight. If the alumina content is less than 40% by weight, the heat resistant temperature of the reinforcing fibers is lowered and the reinforcing fibers may occasionally react with aluminium in the compositing step to degrade the reinforcing fibers.
  • the alumina fibers or alumina-silica-type fibers are used in this invention because these fibers have excellent sliding characteristics such as abrasion resistance, heat resistance and seizure resistance, as well as because they are less degraded through reaction with the molten aluminium alloy.
  • the average diameter for the alumina fibers or alumina-silica-type fibers is defined to be less than 10 11m (microns). If the average diameter is in excess of 10 pm (microns) the desirable surface accuracy cannot be easily obtained, which reduces the sliding performance, increases the amount of abrasion and also lowers the machining properties.
  • Short fibers are preferred for the alumina fibers or alumina-silica-type fibers.
  • Short fibers as used in this invention are those fibers generally having a fiber length of from 0.1 mm to several tens of millimeters, preferably from 0.1 to 40.0 mm.
  • Alumina-silica-type fibers may contain varoius sizes of non-fibrous particles (shots).
  • the content of the non-fibrous particles (shots) in the alumina-silica-type fibers is desirably not more than 17% by weight. Particularly, it is prefered that the content of the non-fibrous particles with a diameter of not less than 150 11 m (microns) is not more than 7%.
  • the volume ratio of the reinforcing fibers ranges from 5 to 15%. If the volume ratio is less than 5%, the reinforcing fiber is insufficient to suppress the thermal expansion coefficient and the thermal expansion suppressing effect is saturated. Machining properties are also significantly degraded.
  • the volume ratio is defined as the ratio of the reinforcing fibers to the entire fiber reinforced metal composite material which is assumed to be 100 volume %.
  • the reinforcing fibers are preferably disposed in a two-dimensional random manner within a plane parallel to the direction in which suppression of the thermal expansion coefficient is desired. Further, a higher intraplane orientation rate in said plane is better and is preferably not less than 65%. If the intraplane orientation rate is less than 65%, sufficient suppression of the thermal expansion cannot be obtained.
  • the intraplane orientation rate as used herein means the degree of the reinforcing fibers oriented along the plane parallel to the direction along which the thermal expansion is suppressed.
  • the intraplane orientation rate is determined by dividing the number of reinforcing fibers crossing an optional plane in an area reinforced with the reinforcing fibers and having an aspect ratio (i.e., the ratio of the length to breadth of an elliptic cross fiber section which crosses the optional plane) of 3 or more by the total number of the fibers that cross the optional plane, and multiplying the resulting quotient by 100. That is, the intraplane orientation rate is expressed as:
  • the alumina fibers or alumina-silica-type fibers can be oriented in a two-dimensional random manner by using known methods.
  • oriented fibers can be formed by dispersing the fibers in water, alcohol or other similar liquids and sucking the liquid under reduced pressure by forming of a vacuum.
  • the fibers can be oriented by a pressurizing process for pressing the fibers contained within a mold from one direction by urging with a punch.
  • the metal matrix used herein is a hyper-eutectic aluminium-silicon-type alloy enriched in primary crystal silicon which is hard grains. Hyper-eutectic aluminium silicon-type alloys are preferred, for increasing the amount of the primary crystal silicon.
  • the aluminium-silicon-type alloy used in this invention includes 15 to 30% by weight of silicon.
  • A-390 alloy containing about 17% silicon by weight can be used.
  • the A-390 alloy comprises a composition of aluminium, 16 ⁇ 18% silicon and a small amount of magnesium. It is also preferable to increase the magnesium content further from that in the A-390 alloy.
  • the amount of magnesium in the matrix can be from 0.5 to 0.8% by weight. The magnesium content is increased, because the alumina-silica-type fibers or alumina fibers are liable to react with magnesium and thereby reduce the magnesium content in the matrix and, therefore, the amount of magnesium is compensated for initially.
  • the particle size of the primary crystal silicon which is hard grains is preferably not more than 52 11 m (microns) and, more preferably, not more than 40 11m (microns) in average particle size.
  • the maximum particle size of the primary crystal silicon is desirably not more than 80 11m (microns).
  • the particle size of the primary crystal silicon is given as described above, because if the particle size of the primary crystal silicon is larger, cracking is liable to occur within the primary crystal silicon. If cracking occurs, the primary crystal silicon is liable to be broken and the cracked primary crystal silicon will bite into the sliding surface producing undesirable effects on the sliding movement.
  • the particle size of the primary crystal silicon is larger, primary crystal silicon of larger particle sizes tend to surround the reinforcing fibers thereby causing cracking due to differences in the rigidity and heat expansion coefficients between the primary crystal silicon and the reinforcing fibers. Accordingly, it is desirable to minimize the particle size of the primary crystal silicon in order to suppress the cracking of the primary crystal silicon.
  • the primary crystal silicon For reducing the particle size of the primary crystal silicon, it is desirable to employ a production process in which the molten aluminium-silicon-type alloy is impregnated to bring the alloy in contact with the fiber assembly, molded from reinforcing fibers into a predetermined configuration. Since the molten alloy is cooled in contact with the fibers, the primary crystal silicon can be prevented from growing coarser.
  • the method of impregnating the molten alloy between the reinforcing fibers, as described above, can include conventionally employed processes such as the liquid metal forging cast process, the high pressure casting process and the molten alloy permeating process.
  • the particle size of the primary crystal silicon generally depends on the cooling rate of the molten alloy and the particle size can be varied by adjusting variables such as the temperature of the molten alloy, the pre-heating temperature of the reinforcing fibers and the pressure of the molten alloy. For instance, if the pre-heating temperature of the reinforcing fibers is set to 400°C, the average particle size of the primary crystal silicon can be reduced to about 24 ⁇ m (microns).
  • the fiber assembly When using the liquid metal forging cast process or the high pressure casting process, since the molten alloy is impregnated between the reinforcing fibers while being under a pressure of from 19.6 to 98.1 MPa (200 to 1,000 kg/cm 2 ), it is desirable for the fiber assembly to have a sufficient strength to withstand the compressing force from the molten alloy. Accordingly, it is desirable for the fiber assembly to have a high compression strength of more than 19.6 kPa (0.2 kg/cm 2 ) and preferably, more than 49.0 kPa (0.5 kg/cm 2 ).
  • the reinforcing fibers For improving the compression strength of the fiber assembly, it is preferable to bond the reinforcing fibers with an inorganic binder that does not significantly lose its bonding strength even when in contact with the molten alloy at high temperature.
  • the inorganic binder of this invention can include colloidal silica, colloidal alumina, water glass, cement and alumina phosphate solution.
  • the fiber assembly is formed by dispersing the reinforcing fibers in the inorganic binder, stirring the liquid mixture, forming the assembly of the fibers from the reinforcing fibers in the liquid mixture through a vacuum forming process and then, drying or sintering them.
  • test piece A is shown in Figure 4, test piece B in Figure 5, test piece C in Figure 6, and test piece D in Figure 7.
  • large grey particle portions represent primary crystal silicon and black circular and elliptic portions represent reinforcing fibers. Sliding tests at a high surface pressure were carried out on the test specimens A-D.
  • the abrasion characteristics were examined by forming blocks each of 6.35 mmx10.16 mmx15.7 mm from the test specimens A-D, bringing a ring made of bearing steels SUJ-2 (35 mm outer diameter) into contact with the block under a load of 1.47 kN (150 kg), and rotating the ring at 160 min- 1 for one hour in this state.
  • Castle motor oil 5W-30 was continuously supplied as the lubricant oil during the test.
  • test results for the abrasion are shown in Figure 8.
  • excess abrasion resulted in test piece D which had a primary crystal silicon of 63 11 m (microns) average particle size.
  • excess abrasion was also observed in the mating material of test piece D.
  • the abrasion was low in the test specimens A-C. Accordingly, as is apparent from Figure 8, it is desirable to limit the particle size of primary crystal silicon to not more than about 60 11m (microns) in order to reduce the amount of abrasion.
  • cracking in the primary crystal silicon was examined for each of the blocks after the sliding test. Cracking resulted in all of the cases where the particle size of the primary crystal silicon was greater than 80 11m (microns).
  • Application Example 1 shown in Figure 9 illustrates the case where the fiber reinforced metal composite material according to this invention was applied to a vane of a rotary type compressor for use in an air conditioner.
  • alumina-silica-type fibers with an average diameter of 3 11m (microns) and a length of 1.0-2.5 mm (trade name Kaowool, manufactured by Isolight Bubcock Refractory Company) were removed with non-fibrous particles and mixed with a water soluble silica sol as an inorganic binder. Then, a platelike fiber assembly of 40 mmx70 mmx10 mm dimensions was molded by way of a vacuum forming process. The fiber assembly had a bulk density of 0.18 glcm 3 and a fiber volume ratio of 7%. The fibers in the fiber assembly were oriented at random in a.
  • Fiber assembly 103 was then contained within cavity 102a of molding die 102 comprising main die 100 and upper die 101 to which was rapidly poured molten metal 104 of a hyper-eutectic aluminium-silicon-type alloy.
  • the molten metal had a composition of AI-17% Si-4% Cu-0.8% Mg and a molten metal temperature of 790°C.
  • the molten alloy contained a larger amount of magnesium than that in the usually employed A-390 alloy.
  • the magnesium content is increased since the alumina-silica-type fibers and magnesium are liable to react with each other reducing the magnesium contained in the matrix at the stage of the heat treatment in the subsequent step.
  • the fiber reinforced metal composite material prepared as described above ws heat treated (T6), and then machined to a predetermined shape into vanes 3a and 3b as shown in Figure 9. Vanes 3a and 3b had a thermal expansion coefficient of 16 ⁇ 10 -6 /°C, which was lower than the thermal expansion coefficient of the usually employed A-390 alloy (18 ⁇ 19 ⁇ 10 -6 /°C).
  • the compressor shown in Figure 9 is a through vane type coolant compressor in which circular rotor 2 made of cast iron is rotatably disposed within circular main body 1 made of cast iron.
  • Compression chamber 3 whose cross sectional area changes continuously is formed between the main body (1) and the rotor (2), and intake port 11 for sucking coolant from the side of the evaporator not illustrated is opened to a portion of the main body (1) corresponding to a portion where the volume of the compression chamber (3) is increased.
  • discharge port 12 for discharging the coolant is formed at a portion of the main body (1) corresponding to the portion where the volume of the compression chamber (3) is most decreased.
  • Guide grooves 21 and 22 are formed in rotor 2 such that they penetrate in the diametrical direction and are perpendicular to each other.
  • Vanes 3a and 3b are inserted slidably to the guide grooves (21 and 22 respectively). Accordingly, the liner portion 13 has a specific profile along which both ends of vanes 3a and 3b can always move slidingly. Further, the width of vanes 3a and 3b are formed substantially to the same size as the gap of liner side portion 14forming both of the side walls of the compression chamber (3). When the ceompressor is operated, vanes 3a and 3b generate heat due to the sliding friction between the vanes (3a, 3b) and the liner portion (13) and due to the adiabatic compression of gas.
  • the thermal expansion coefficient can be decreased to 16x10- 6 /°C. Accordingly, the clearance between the vanes (3a, 3b) and the liner portion (13), and the clearance between the vanes (3a, 3b) and the liner side portion (14) can be decreased as compared with conventional vanes. Therefore, the size of the clearance can be narrowed by design as compared with the conventional vane. Accordingly, in the case of using vanes 3a and 3b of this embodiment, the volume efficiency of the compressor is from about 81 to 83%, which can be improved by about 3% as compared with the conventional volume efficiency of from 79 to 81 %.
  • a duration test was effected for the compressor incorporating vanes 3a and 3b as described above.
  • the duration test consisted of (i) a continuous duration test, (ii) a liquid compression test and (iii) a gas lacking test.
  • the continuous duration test was effected by continuously rotating the compressor for 100 hours.
  • the liquid compression test was carried out by liquefying the coolant and applying an impulsive load on it.
  • the gas lacking test was effected while decreasing the amount of the coolant. Since the vanes (3a, 3b) were excellent in abrasion resistance, heat resistance and seizure resistance as described above, the test results were satisfactory for all of the tests.
  • the fiber reinforced metal composite material can also be used as a vane for a movable blade vane compressor as shown in Figure 11.
  • Bottomed grooves 23, 24, 25, and 26 are formed radially to rotor 20 in a compressor as shown in Figure 11, and vanes 3c, 3d, 3e and 3f are slidably inserted to the respective grooves (23, 24, 25 and 26).
  • spaces 41, 42, 43 and 44 are formed between the bottom face for each of the vanes (3c-3f) and the bottom face for each of the grooves (23-26), such that compressed liquid from fluid channel 3 is introduced upon operation.
  • the top ends of the vanes (3c-3f) are urged to the liner portion 13 with the pressure by the compressed liquid.
  • the fiber assembly with a bulk density of 0.5 g/cm 3 and a fiber volume ratio of 14.3% was prepared by using alumina fibers (Saffaile made by ICI Co.) of 3 11 m (micron) diameter and 1.5 mm length.
  • the metal is melted and composited to the fiber assembly, thereby forming them into a vane component for use in a compressor.
  • the molten metal alloy comprises an AI-18% Si-2% Cu-1 % Mg-1.5% Ni alloy.
  • the molten metal temperature was set to 800°C and the fiber assembly has a pre-heating temperature of 600°C.
  • the vane component manufactured from the fiber reinforced metal composite material as described above has a heat expansion coefficient of 15.2x 10 -6 /°C.
  • the vane material was then subjected to machining after the heat treatment, and the vane was incorporated into a rotary compressor as shown in Figure 9, in the same manner as in Application Example 1.
  • the volume efficiency of the compressor can also be improved by 5%. Satisfactory results are also obtained with the continuous duration test, the liquid compression test and the gas lacking test as described above.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Cylinder Crankcases Of Internal Combustion Engines (AREA)
  • Compressor (AREA)
  • Compressors, Vaccum Pumps And Other Relevant Systems (AREA)
  • Applications Or Details Of Rotary Compressors (AREA)
EP19850115192 1985-01-21 1985-11-29 Fiber reinforced metal composite material Expired - Lifetime EP0188704B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP8894/85 1985-01-21
JP889485A JPH0696188B2 (ja) 1985-01-21 1985-01-21 繊維強化金属複合材料

Publications (3)

Publication Number Publication Date
EP0188704A2 EP0188704A2 (en) 1986-07-30
EP0188704A3 EP0188704A3 (en) 1988-01-13
EP0188704B1 true EP0188704B1 (en) 1991-02-06

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EP19850115192 Expired - Lifetime EP0188704B1 (en) 1985-01-21 1985-11-29 Fiber reinforced metal composite material

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US (1) US4696866A (ja)
EP (1) EP0188704B1 (ja)
JP (1) JPH0696188B2 (ja)
DE (1) DE3581723D1 (ja)

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JPS5534215B2 (ja) * 1974-02-08 1980-09-05
FR2343895A1 (fr) * 1976-03-10 1977-10-07 Pechiney Aluminium Procede de fabrication de corps creux en alliages d'aluminium au silicium par filage de grenailles
JPS57131333A (en) * 1981-02-04 1982-08-14 Tokai Daigaku Reducing method for grain size of proeutectic silicon of hypereutectic aluminum-silicon alloy
DE3268826D1 (en) * 1981-09-01 1986-03-13 Sumitomo Chemical Co Method for the preparation of fiber-reinforced metal composite material
JPS5893837A (ja) * 1981-11-30 1983-06-03 Toyota Motor Corp 複合材料及びその製造方法
CA1213157A (en) * 1981-12-02 1986-10-28 Kohji Yamatsuta Process for producing fiber-reinforced metal composite material
FR2528910B1 (fr) * 1982-06-17 1986-12-12 Cegedur Chemises de moteurs a base d'alliages d'aluminium et de grains de silicium calibres et leurs procedes d'obtention
DE3344687A1 (de) * 1983-12-10 1984-10-18 Daimler-Benz Ag, 7000 Stuttgart Kolben aus magnesium oder einer magnesiumlegierung fuer brennkraftmaschinen

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DE3581723D1 (de) 1991-03-21
US4696866A (en) 1987-09-29
EP0188704A3 (en) 1988-01-13
JPH0696188B2 (ja) 1994-11-30
EP0188704A2 (en) 1986-07-30
JPS61169154A (ja) 1986-07-30

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